CN112301283A - Precipitation hardening austenitic alloy steel with high expansibility and thermal stability and method for manufacturing same - Google Patents

Precipitation hardening austenitic alloy steel with high expansibility and thermal stability and method for manufacturing same Download PDF

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CN112301283A
CN112301283A CN202011193750.7A CN202011193750A CN112301283A CN 112301283 A CN112301283 A CN 112301283A CN 202011193750 A CN202011193750 A CN 202011193750A CN 112301283 A CN112301283 A CN 112301283A
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CN112301283B (en
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杨旗
王敏
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Shanghai Material Research Institute Co ltd
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Shanghai Institute of Materials
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

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  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The present invention relates to a precipitation hardening austenitic alloy steel having high expansibility and thermal stability and a method for manufacturing the same. The chemical components by mass percent are as follows: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent. The austenitic alloy steel is prepared by the technological processes of fusion casting, forging or hot rolling or forging cogging and hot rolling and solution aging treatment, and the linear expansion coefficient alpha of the austenitic alloy steel ism(25,400)≥16.5×10‑6The room temperature hardness is not less than 36HRC at the temperature of/° C, and is not less than 34HRC after heat preservation is carried out for 24 hours at the temperature of 700 ℃.

Description

Precipitation hardening austenitic alloy steel with high expansibility and thermal stability and method for manufacturing same
Technical Field
The invention belongs to the technical field of high-strength steel, and particularly relates to precipitation hardening type austenitic alloy steel with high expansibility and thermal stability and a manufacturing method thereof.
Background
The mechanical manufacturing industry is continuously developing towards high efficiency and high precision of processing and manufacturing. Mechanical equipment components (such as numerically controlled machine tool system clamping tool handles, transmission shafts, etc.) are increasingly using high-strength and ultra-high-strength steel materials. The matched parts can be tightly connected through a hot-fitting method, so that the mechanical equipment is compact in structure and high in operation safety and machining precision. Here, the components that are mated with each other are referred to as a containing member and a contained member, respectively. For example, a hot-set tool holder (containing part, usually made of high-strength steel) for a high-speed numerical control machine tool is widely applied due to the advantages of high clamping precision, large clamping force, large bending rigidity, good dynamic balance performance and the like of a machining tool (contained part), and the use of the hot-set tool holder is beneficial to improving the cutting machining efficiency and prolonging the service lives of a machine tool spindle and the machining tool.
The hot-fitting method is to realize the assembly connection by using the difference of the thermal expansion coefficients of the containing piece material and the contained piece material. At room temperature, the aperture of the containing part is smaller than the outer diameter of the contained part. During the assembling process, the containing part is heated, the clamping hole diameter of the containing part is enlarged due to thermal expansion, the contained part can be smoothly placed in the hole diameter of the containing part, and the containing part is cooled and then contracted and is connected with the contained part in an extruding way. Thus, the containment element is generally required to have good thermal expansion characteristics (i.e., a high coefficient of expansion) while having high strength. When the container is disassembled, the container and the contained part are heated simultaneously, and the contained part can be taken out easily because the thermal expansion coefficient of the material of the container is higher than that of the material of the contained part and the aperture of the container is larger than the outer diameter of the contained part at high temperature. For parts that require repeated assembly and disassembly, the enclosure material also needs to have good high temperature oxidation resistance and thermal stability (i.e., the strength of the material does not significantly decay with multiple cycles of heating of the enclosure) to maintain the precision of the hot assembly of the parts.
At present, most of materials used as hot assembly containing parts in mechanical equipment are hot-work die steel (such as 4Cr5MoSiV1) and common high-strength heat-resistant stainless steel. The materials have low thermal expansion coefficient, poor high-temperature oxidation resistance and/or poor thermal stability, which can cause that plastic deformation and material surface oxidation are easy to occur on the containing piece due to overhigh assembling temperature during hot assembly, and the material strength is obviously attenuated after being assembled and disassembled for many times, thereby reducing the assembling precision, the operation safety and the processing precision of mechanical equipment. Therefore, there is an urgent need to develop a high-strength steel material having high expansion properties, high-temperature oxidation resistance and thermal stability for manufacturing a hot-fitting housing in mechanical equipment.
Disclosure of Invention
The present invention has been made to overcome the above-mentioned drawbacks of the prior art and an object of the present invention is to provide a precipitation hardening austenitic alloy steel having high expansibility and thermal stability and a method for manufacturing the same.
In order to achieve the purpose, the technical scheme of the invention is as follows:
in a first aspect, the present invention provides a precipitation hardening austenitic alloy steel having high expansion and thermal stability.
To obtain a high linear expansion coefficient, the alloy steel matrix structure needs to be a single austenite structure. In the present invention, austenite forming elements of C, Ni, Mn, and Cu are added and the contents of ferrite forming elements of Cr, Mo, Al, and Si are controlled so that the alloy steel matrix has a single austenite structure.
In order to obtain high strength and good thermal stability, fine second phase hard particles need to be uniformly dispersed in a matrix of the alloy steel, and the second phase hard particles are not remarkably coarsened in the process that the alloy steel is kept at 700 ℃ for 24 hours. Adding a proper amount of carbide forming elements such as Nb, V, Cr, etc. into steel, and performing solid solution and aging treatment to combine part of C with Nb, V, Cr to form MX-type carbide and carbonitride (having face-centered cubic crystal structure) and Cr in austenite matrix23C6And the phases are precipitated, thereby improving the strength of the alloy steel. The fine-scale MX phase has good thermal stability, and can improve the high-temperature strength and the thermal stability of the alloy steel. In addition, C, Si and Mo have good solid solution strengthening effect, and can obviously improve the strength (at high temperature and room temperature) of the steel.
In order to provide the alloy steel with good high-temperature oxidation resistance, the alloying elements comprise Al, Si and Cr elements. By forming dense Al on the surface of the steel2O3、Cr2O3、SiO2Or a composite oxide layer, which reduces the oxidation speed of the steel at high temperature.
In order to make the alloy steel have better corrosion resistance, proper amounts of Cr, Ni, Cu and Mo elements are required to be added.
Specifically, the precipitation hardening type austenitic alloy steel with high expansibility and thermal stability comprises the following chemical components in percentage by mass: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent.
Preferably, in the precipitation hardening type austenitic alloy steel with high expansibility and thermal stability, the mass percentages of C, Cr, V, Nb, Mo and Cu elements are as follows: c is more than or equal to 0.45 percent and less than or equal to 0.65 percent, Cr is more than or equal to 9.0 percent and less than or equal to 12.0 percent, Mo is more than or equal to 1.5 percent and less than or equal to 3.0 percent, Cu is more than or equal to 1.5 percent and less than or equal to 3.0 percent, V is more than or equal to 0.8 percent and less than or equal to 1.2 percent, and Nb is more than or equal to 0.15 percent and.
Further, the matrix structure of the precipitation hardening type austenitic alloy steel with high expansibility and thermal stability is a single austenitic structure and second phase particles dispersed and distributed in the austenitic matrix;
the second phase particles are mainly MX type carbides and carbonitrides formed between C element and V, Nb element and carbides formed between C element and Cr element.
The precipitation hardening type austenitic alloy steel with high expansibility and thermal stability has the characteristics of high strength, high thermal expansion coefficient, good high-temperature oxidation resistance and thermal stability, good corrosion resistance and the like, and the physical and mechanical properties of the alloy steel meet the following requirements: coefficient of linear expansion alpham(25,400)≥16.5×10-6The room temperature hardness is not less than 36HRC, and the room temperature hardness is not less than 34HRC after heat preservation is carried out for 24 hours at 700 ℃.
In the composition design of the precipitation hardening type austenitic alloy steel having high expansibility and thermal stability according to the present invention, the respective components function as follows.
C: c is a strong austenite stabilizing element. C can significantly improve the strength of steel by solid solution strengthening. In addition, C combines with Nb, V, Cr elements to form finely dispersed second phase particles, i.e., carbides and carbonitrides (MX-type) and Cr in the matrix of the steel23C6The carbides are made to improve the strength of the alloy steel by precipitation strengthening. When the C content is lower than 0.35%, the volume fraction of precipitated second phase particles in the steel is small, so that the room temperature hardness of the steel is often lower than 36HRC, and the thermal stability of the steel is poor; in addition, a ferrite phase is likely to occur in the matrix structure of the alloy steel. When the content of C is too high, workability and corrosion resistance of the alloy steel may be deteriorated. Therefore, the carbon content is controlled to be 0.35-1.0%, and the carbon content is preferably 0.45-0.65%.
Si: si is an important element for improving the high-temperature oxidation resistance of the alloy steel in the invention. On the one hand, the addition of Si can promote surface Cr2O3On the other hand, SiO2The oxide layer reduces the diffusion speed of iron atoms and oxygen atoms, slows down the oxidation process of the steel, and thus improves the oxidation resistance of the steel. Si can effectively perform a solid solution strengthening function. However, when the Si content is too high, the plasticity and weldability of the alloy steel are reduced; and excessive Si is not beneficial to increase the thermal expansion coefficient of the alloy steel. The invention controls the content of Si not more than 3.0%.
Al: al is an important element for improving the high-temperature oxidation resistance of the alloy steel in the invention. The addition of Al can promote the formation of the filmSurface Al2O3The oxidation process of the steel is effectively delayed, so that the oxidation resistance of the steel is improved. In addition, Al can combine with Ni to form fine intermetallic particles, which act to strengthen the austenitic matrix. However, when the Al content is excessively high, the plasticity, welding properties, and manufacturability of the alloy steel may be reduced. The invention controls the Al content not to be more than 3.0 percent.
In the invention, the contents of Si and Al are controlled to simultaneously satisfy: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent. When Al + Si is less than 0.8%, the two elements are not obvious in improving the high-temperature oxidation resistance of the alloy steel; when Al + Si > 4.0%, the plasticity, weldability, and manufacturability of the alloy steel are significantly reduced.
Mn: mn is an austenite stabilizing element and can partially replace a noble metal element Ni so as to ensure a single austenite structure of the alloy steel and reduce the cost of steel grades. In addition, Mn is easily combined with S in steel to form MnS, and the machinability of the alloy steel can be improved. However, too high Mn content may reduce corrosion resistance and weldability of the alloy steel. The invention controls the Mn content to be 3.0-15.0%.
Cr: cr is an important element for improving corrosion resistance and high-temperature oxidation resistance of alloy steel, and can be combined with C to form Cr in a matrix of the steel23C6And carbide is added, so that the strength and the hardness of the alloy steel are increased. The Cr content is too low, and the corrosion resistance and the high-temperature oxidation resistance of the alloy steel are poor. However, Cr is a ferrite-forming element, and an excessively high Cr content tends to form ferrite in the steel, thereby lowering the thermal expansion coefficient of the steel. The invention controls the Cr content to be 7.0-15.0%, preferably 9.0-12.0%.
Ni: ni is an austenite stabilizing element, which is beneficial to the alloy steel matrix to obtain a single austenite structure, so that the steel grade keeps good ductility and toughness. Ni can promote the stability of the Cr-containing passive film, thereby improving the corrosion resistance and high-temperature oxidation resistance of the alloy steel. Ni also improves the corrosion resistance of the steel in alkaline media. Furthermore, Ni can combine with Al to form fine intermetallic compound particle phase, which acts to strengthen the austenite matrix. However, Ni is a precious alloy element, and adding too much Ni can significantly increase the cost of the alloy; moreover, increasing the Ni content is not beneficial to improving the thermal expansion coefficient of the alloy steel. The invention controls the Ni content to be 2.0-10.0%.
Mo: mo can improve the reducing medium corrosion resistance, pitting corrosion resistance and crevice corrosion resistance of the alloy steel, and is dissolved in an austenite matrix to improve the strength and the thermal stability of the alloy steel, but the Mo is expensive so as to increase the production cost. The content of Mo is controlled to be 0.5-4.0%, and the content of Mo is preferably 1.5-3.0%.
Cu: cu is an austenite forming element and can partially replace a noble element Ni. When the Cu content is in supersaturation, the alloy steel matrix is converged to form a copper-rich phase after the solution aging treatment, and then the room temperature strength and the high temperature strength of the steel are improved. In addition, the addition of Cu is effective in improving the corrosion resistance of alloy steel and reducing the cold work hardening tendency of steel. However, too much Cu significantly reduces the hot workability of the steel. Therefore, the Cu content is controlled to be 0.5-4.0%, and the Cu content is preferably 1.5-3.0%.
Nb and V: nb and V are strong carbide and/or carbonitride forming elements, and form a fine MX type second phase by combining with C, N element, which can significantly improve the strength and thermal stability of the alloy steel. In addition, since Nb and V preferentially combine with carbon in steel, Cr in steel is reduced23C6And (4) the precipitation of carbides, thereby improving the corrosion resistance of the steel. Moreover, the addition of Nb can well play a role in grain refinement. When the Nb and V content is too low (0.7Nb + V is less than 0.65%), the content of precipitated second phase is less, and the room temperature hardness of the alloy steel is not more than 36 HRC; when the Nb and V content is too high (0.7Nb + V is more than 2.5%), a large amount of second phase is precipitated, and the ductility and toughness of the alloy steel are obviously reduced. In the invention, the Nb content is controlled to be 0.08-1.0 percent, the V content is controlled to be 0.4-2.0 percent, and the Nb content and the V content also need to meet the following requirements: 0.65 percent to 0.7 percent of Nb + V to 2.5 percent, preferably 0.15 percent to 0.5 percent of Nb and 0.8 percent to 1.2 percent of V.
In the invention, the Nb and V composite addition mode is adopted, and the effects of grain refinement and precipitation hardening can be effectively achieved at the same time. Moreover, the effect of the Nb and V composite addition is larger than the effect of the Nb or V element addition alone. In addition, the cost of the alloy steel can be reduced by adopting the Nb and V composite addition (the addition amount of V is properly reduced), and the production and manufacturing process window of steel grades can be properly enlarged.
N: n is easy to combine with Al to generate AlN inclusions in the matrix of the steel, thereby influencing the manufacturability and ductility of the alloy steel. The invention limits N to be less than or equal to 0.03 percent.
P: p increases the cold shortness of the steel and reduces the formability and weldability of the steel. The invention controls P to be less than or equal to 0.02 percent.
S: s can cause the steel to generate hot brittleness, and reduce the plastic toughness and the welding performance of the steel; however, the inclusion of an appropriate amount of MnS in the steel contributes to enhancing the cutting performance thereof. The invention controls the S to be less than or equal to 0.10 percent.
In the invention, the contents of C, Ni, Mn and Cu elements are controlled to ensure that the matrix structure of the alloy steel is a single austenite structure and maintain the excellent thermal expansion performance (linear expansion coefficient alpha) of the alloy steelm(25,400)≥16.5×10-6/° c). Moreover, the component design reduces the content of Ni element as much as possible so as to reduce the cost of the alloy steel. The alloy steel of the invention is rich in Si, Al and Cr elements, so the alloy steel has good high-temperature oxidation resistance. In addition, the alloy steel has proper corrosion resistance because of addition of Cr, Ni, Cu and Mo elements.
In a second aspect, the present invention provides two types of methods for manufacturing the above precipitation hardening austenitic alloy steel having high expansibility and thermal stability.
A method for manufacturing a first type of precipitation hardening austenitic alloy steel with high expansion and thermal stability, comprising the steps of:
1) smelting and casting according to the following component proportion to obtain a casting blank
The mass percentage of the chemical components is as follows: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent.
2) Thermal deformation processing
Heating the casting blank at 1050-1230 ℃, preserving heat for 1-6 h, and then thermally processing the casting blank into a bar or a plate.
3) Post-deformation heat treatment
The post-deformation heat treatment comprises two procedures of solution treatment and aging treatment, wherein the solution treatment is firstly carried out on the bar or plate after the hot working deformation, and then the aging treatment is carried out on the material after the solution treatment.
Preferably, in the step 2), the thermal deformation processing mode is hot rolling or forging, the deformation pass temperature is more than or equal to 850 ℃, and the ratio of the cross sectional area of the casting blank before and after thermal deformation is more than or equal to 2.0.
Preferably, in step 3), the conditions for solution treatment are: the solid solution temperature is 1150-1230 ℃, the temperature is kept for 1-5 h, and then the mixture is cooled to the room temperature at the cooling speed of not less than 300 ℃/min.
Preferably, in step 3), the aging treatment is performed under the following conditions: the aging temperature is 600-750 ℃, the temperature is kept for 2-50 h, and then the air cooling is carried out to the room temperature.
The manufacturing method of the precipitation hardening type austenitic alloy steel having high expansibility and thermal stability according to the first aspect of the present invention is designed for the following reasons:
(1) thermal deformation processing technology
And processing the alloy steel casting blank into a bar or a plate with the required dimension specification through a forging or hot rolling deformation mode.
The heating temperature is 1050-1230 ℃. When the heating temperature exceeds 1230 ℃, the casting blank is over-burnt, and the grain structure of the casting blank is coarse, so that the hot workability is reduced; when the heating temperature is less than 1050 ℃, the degree of homogenization of the structure of the cast slab is insufficient and the deformation resistance of the cast slab is excessive, so that it is difficult to manufacture a plate or bar having a predetermined size without surface defects.
The heating and heat preservation time is 1-6 h. The heat preservation time exceeds 6h, the internal grain structure of the casting blank is coarse, and the production efficiency is influenced; the heat preservation time is less than 1h, the internal temperature of the casting blank is not uniform, and the homogenization degree of the casting blank structure is insufficient.
The ratio of the cross sectional area of the casting blank before and after thermal deformation needs to be controlled to be more than or equal to 2.0 so as to eliminate the nonuniformity and the defects of the internal structure of the casting blank; the hot working of the casting blank is completed by controlling the deformation pass temperature to be more than 850 ℃, and the excessively low deformation pass temperature causes excessively high deformation resistance of the blank, so that the hot-working deformed material with the required dimension specification and without surface and edge defects is difficult to manufacture.
(2) Solution and aging heat treatment
The solid solution and aging treatment are key procedures for obtaining the specified mechanical properties of the alloy steel. And (2) carrying out solution treatment on the bar or plate after hot working (namely, heating the alloy steel to a high-temperature single-phase region, keeping the constant temperature, fully dissolving second-phase particles into the solid solution, and then rapidly cooling to obtain a supersaturated solid solution of the alloy steel), wherein the solution temperature is 1150-1230 ℃, the temperature is kept for 1-5 h, and then the bar or plate is cooled to room temperature at a cooling speed of not less than 300 ℃/min. When the solid solution temperature is lower than 1150 ℃ and the holding time is less than 1h, the second phase particles formed in the prior solidification and hot working processes in the alloy steel can not be mostly or completely dissolved in the austenite matrix, which leads to that the fine second phase particles (MX type and Cr type) with sufficient volume content and dispersed distribution are difficult to precipitate in the austenite matrix during the subsequent aging process of the material due to the lower supersaturation degree of Cr, Nb and V in the austenite23C6Etc.), thereby the alloy steel can not obtain required strength, hardness (the room temperature hardness is more than or equal to 36HRC) and good high-temperature thermal stability (the room temperature hardness is more than or equal to 34HRC after the alloy steel is kept at 700 ℃ for 24 h); while leaving behind coarse second phase particles formed during solidification and hot working that reduce the ductility of the steel alloy. When the cooling speed after solid solution is less than 300 ℃/min, the second phase particles precipitated in the cooling process can be coarsened, and the improvement of the strength and the high-temperature thermal stability of the alloy steel is also not facilitated. When the solid solution temperature is higher than 1230 ℃ and the heat preservation time is too long, the crystal grains of the alloy steel grow rapidly in the solid solution process, and the coarse microstructure can be unfavorable for the strength and the plasticity and toughness of the alloy steel. In addition, too long a solution time affects production efficiency. In actual production, the solid solution temperature can be properly increased to reduce the solid solution heat preservation time.
And (2) carrying out aging treatment on the material after the solution treatment (namely, placing a supersaturated solid solution of the alloy steel at a certain temperature to ensure that the supersaturated solid solution of the alloy steel is subjected to desolventizing and fine second phase precipitation so as to improve the strength of the alloy steel), wherein the aging temperature is 600-750 ℃, keeping the temperature for 2-50 h, and then air cooling to room temperature. The aging temperature is lower than 600 ℃ and the heat preservation time is less than 2h, the volume content of a second phase precipitated in an alloy steel matrix is less, and the strength of the alloy steel is lower; the aging temperature is higher than 750 ℃ and the aging time is too long, the second phase particles are rapidly precipitated and coarsened at a higher temperature, and the precipitation strengthening effect is weakened. In addition, the aging time is too long, which affects the production efficiency. In actual production, the aging temperature can be properly increased to reduce the aging holding time. The aging time is controlled not to exceed 50 h.
A second group of precipitation hardening austenitic alloy steels with high expansion and thermal stability is manufactured by a method comprising the steps of:
1) smelting and casting according to the following component proportion to obtain a casting blank
The mass percentage of the chemical components is as follows: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent.
2) Thermal deformation processing
The hot working comprises two parts of forging cogging and hot rolling, wherein the forging cogging treatment is firstly carried out, and then the hot rolling treatment is carried out.
3) Post-deformation heat treatment
The post-deformation heat treatment comprises two procedures of solution treatment and aging treatment, wherein the solution treatment is firstly carried out on the bar or plate after the hot working deformation, and then the aging treatment is carried out on the material after the solution treatment.
Preferably, in the step 2), the conditions for performing the forging and cogging treatment are as follows: heating a casting blank at 1050-1230 ℃, preserving heat for 1-6 h, and then forging the casting blank into a plate blank or a square blank, wherein the forging deformation pass temperature is more than or equal to 850 ℃, and the ratio of the cross sectional areas of the casting blank before and after forging is more than or equal to 1.5.
Preferably, in the step 2), the conditions for performing the hot rolling treatment are as follows: heating the forging stock at 1050-1230 ℃, preserving heat for 1-6 hours, and then hot rolling the forging stock into a plate or a bar. The hot rolling deformation pass temperature is more than or equal to 850 ℃, and the ratio of the cross section area of the original casting blank to the cross section area of the hot rolled plate or bar is more than or equal to 2.0.
Preferably, in step 3), the conditions for solution treatment are: the solid solution temperature is 1150-1230 ℃, the temperature is kept for 1-5 h, and then the mixture is cooled to the room temperature at the cooling speed of not less than 300 ℃/min.
Preferably, in step 3), the aging treatment is performed under the following conditions: the aging temperature is 600-750 ℃, the temperature is kept for 2-50 h, and then the air cooling is carried out to the room temperature.
The manufacturing method of the precipitation hardening type austenitic alloy steel having high expansibility and thermal stability according to the second aspect of the present invention is designed for the following reasons:
(1) thermal deformation processing technology
And processing the alloy steel casting blank into a bar or a plate with the required dimension specification by a deformation mode combining forging cogging and hot rolling.
And during forging and cogging, the heating temperature is 1050-1230 ℃, and the heating and heat preservation time is 1-6 hours. When the heating temperature exceeds 1230 ℃, the casting blank is over-burnt, and the grain structure of the casting blank is coarse, so that the hot workability is reduced; when the heating temperature is less than 1050 ℃, the degree of homogenization of the structure of the cast slab is insufficient, and the deformation resistance of the cast slab is excessive, so that it is difficult to process a forged slab having a prescribed size without surface defects. The heat preservation time exceeds 6h, the internal grain structure of the casting blank is coarse, and the production efficiency is influenced; the heat preservation time is less than 1h, the internal temperature of the casting blank is not uniform, and the homogenization degree of the casting blank structure is insufficient. The ratio of the cross sectional area of the casting blank before and after forging is controlled to be more than or equal to 1.5, so that the nonuniformity and the defects of the internal structure of the casting blank are basically eliminated, and a good rolled blank structure is provided for subsequent hot rolling; the temperature of the forging pass needs to be controlled to be more than 850 ℃, and the excessively low temperature of the forging pass causes excessively high deformation resistance of the blank, so that the forged blank with required dimension specifications and no surface and edge defects is difficult to manufacture.
And during hot rolling, heating the forging stock at 1050-1230 ℃, and keeping the temperature for 1-6 hours. When the heating temperature exceeds 1230 ℃, the forging stock is over-burnt, and the grain structure of the forging stock is coarse, so that the hot working performance of the forging stock is reduced; when the heating temperature is lower than 1050 ℃, the deformation resistance of the forged blank is too large, so that it is difficult to process a bar or plate having a prescribed size without surface defects. The heat preservation time exceeds 6h, the internal grain structure of the forging stock is coarse, and the production efficiency is influenced; the heat preservation time is less than 1h, and the internal temperature of the forging stock is not uniform. The invention controls the hot rolling pass temperature to be more than 850 ℃, and the too low hot rolling pass temperature can cause too high deformation resistance of the material, thereby being difficult to manufacture the bar or the plate with required dimension specification and without surface and edge defects. The ratio of the cross section area of the original casting blank to the cross section area of the hot rolled plate or bar is controlled to be more than or equal to 2.0, so that the hot rolled material is uniform in structure.
The method combining forging cogging and hot rolling is suitable for preparing alloy steel bars or plates with high requirement on structural uniformity and small cross-sectional area, and can improve the utilization rate of materials.
(2) Solution and aging heat treatment
The solid solution and aging treatment are key procedures for obtaining the specified mechanical properties of the alloy steel. And (2) carrying out solution treatment on the bar or plate after hot working (namely, heating the alloy steel to a high-temperature single-phase region, keeping the constant temperature, fully dissolving second-phase particles into the solid solution, and then rapidly cooling to obtain a supersaturated solid solution of the alloy steel), wherein the solution temperature is 1150-1230 ℃, the temperature is kept for 1-5 h, and then the bar or plate is cooled to room temperature at a cooling speed of not less than 300 ℃/min. When the solid solution temperature is lower than 1150 ℃ and the holding time is less than 1h, the second phase particles formed in the prior solidification and hot working processes in the alloy steel can not be mostly or completely dissolved in the austenite matrix, which can cause that the materials are difficult to precipitate dispersion components with enough volume content in the austenite matrix during the subsequent aging process due to the lower supersaturation degree of Cr, Nb and V in the austeniteFine second phase particles of cloth (MX type and Cr23C6Etc.), thereby the alloy steel can not obtain required strength, hardness (the room temperature hardness is more than or equal to 36HRC) and good high-temperature thermal stability (the room temperature hardness is more than or equal to 34HRC after the alloy steel is kept at 700 ℃ for 24 h); while leaving behind coarse second phase particles formed during solidification and hot working that reduce the ductility of the steel alloy. When the cooling speed after solid solution is less than 300 ℃/min, the second phase particles precipitated in the cooling process can be coarsened, and the improvement of the strength and the high-temperature thermal stability of the alloy steel is also not facilitated. When the solid solution temperature is higher than 1230 ℃ and the heat preservation time is too long, the crystal grains of the alloy steel grow rapidly in the solid solution process, and the coarse microstructure is unfavorable for the strength and the plasticity and toughness of the alloy steel. In addition, too long a solution time affects production efficiency. In actual production, the solid solution temperature can be properly increased to reduce the solid solution heat preservation time.
And (2) carrying out aging treatment on the material after the solution treatment (namely, placing a supersaturated solid solution of the alloy steel at a certain temperature to ensure that the supersaturated solid solution of the alloy steel is subjected to desolventizing and fine second phase precipitation so as to improve the strength of the alloy steel), wherein the aging temperature is 600-750 ℃, keeping the temperature for 2-50 h, and then air cooling to room temperature. The aging temperature is lower than 600 ℃ and the heat preservation time is less than 2h, the volume content of a second phase precipitated in an alloy steel matrix is less, and the strength of the alloy steel is lower; the aging temperature is higher than 750 ℃ and the aging time is too long, the second phase is rapidly precipitated and coarsened at higher temperature, and the precipitation strengthening effect is weakened. In addition, the aging time is too long, which affects the production efficiency. In actual production, the aging temperature can be properly increased to reduce the aging holding time. The aging time is controlled not to exceed 50 h.
By adopting the component design, the hot working process and the heat treatment process, the original matrix structure of the prepared alloy steel bar or plate is a single austenite structure, fine second-phase particles are dispersed in the austenite matrix structure, and the second phase mainly comprises carbide, carbonitride (MX type) and Cr23C6. The alloy steel has high strength, good thermal stability and high temperature oxidation resistance, good thermal expansion characteristics and appropriate corrosion resistance. Linear expansion coefficient alpha of alloy steelm(25,400)≥16.5×10-6/° c; the room temperature hardness of the alloy steel is not less than 36HRC, and the room temperature hardness is not less than 34HRC after heat preservation is carried out for 24 hours at 700 ℃.
The precipitation hardening type austenitic alloy steel with high expansibility and thermal stability is suitable for but not limited to manufacturing containers which are repeatedly assembled and disassembled in a hot assembling mode in mechanical equipment, such as hot assembled tool shanks of tool system components of numerical control machines.
Compared with the prior art, the invention has the following beneficial effects:
1. compared with the traditional hot-work die steel and common high-strength heat-resistant stainless steel, the high-strength austenitic alloy steel has high expansion characteristic and linear expansion coefficient alpham(25,400)≥16.5×10-6V. C. In addition, the alloy steel has good high-temperature oxidation resistance, thermal stability and corrosion resistance.
2. The invention uses Mn element to replace Ni partially, which can reduce the cost of alloy steel reasonably.
3. The manufacturing process can be completed on the existing alloy steel production line without large adjustment, so that the invention has good popularization and application prospects.
Detailed Description
A precipitation hardening type austenitic alloy steel with high expansibility and thermal stability comprises the following chemical components in percentage by mass: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent.
A first method of manufacturing the precipitation hardening austenitic alloy steel with high expansion and thermal stability comprises the steps of:
1) smelting and casting according to the following component proportion to obtain a casting blank
The chemical components by mass percent are as follows: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent.
2) Thermal deformation processing
Heating the casting blank at 1050-1230 ℃, preserving heat for 1-6 h, and then thermally processing the casting blank into a bar or a plate. The hot deformation processing mode is hot rolling or forging. The deformation pass temperature is more than or equal to 850 ℃, and the ratio of the cross-sectional areas of the casting blank before and after thermal deformation is more than 10.
3) Post-deformation heat treatment
The post-deformation heat treatment comprises two procedures of solution treatment and aging treatment. Firstly, carrying out solution treatment on the bar or plate subjected to hot working deformation, wherein the solution temperature is 1150-1230 ℃, preserving the heat for 1-5 h, and then cooling to room temperature at a cooling speed of not less than 300 ℃/min. And carrying out aging treatment on the material subjected to the solution treatment, wherein the aging temperature is 600-750 ℃, keeping the temperature for 2-50 h, and then air-cooling to room temperature.
A second method of manufacturing the precipitation hardening austenitic alloy steel with high expansion and thermal stability comprises the steps of:
1) smelting and casting according to the following component proportion to obtain a casting blank
The chemical components by mass percent are as follows: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent.
2) Thermal deformation processing
The hot working comprises two parts of forging and cogging and hot rolling.
And heating the casting blank at 1050-1230 ℃, preserving heat for 1-6 hours, and then forging the casting blank into a plate blank or square blank. The forging deformation pass temperature is more than or equal to 850 ℃, and the ratio of the cross sectional areas of the casting blank before and after forging is more than 3;
heating the forging stock at 1050-1230 ℃, preserving heat for 1-6 hours, and then hot rolling the forging stock into bars or plates. The hot rolling deformation pass temperature is more than or equal to 850 ℃, and the ratio of the cross section area of the original casting blank to the cross section area of the hot rolled plate or bar is more than or equal to 12.
3) Post-deformation heat treatment
The post-deformation heat treatment comprises two procedures of solution treatment and aging treatment. Firstly, carrying out solid solution treatment on the bar or plate after hot working, wherein the solid solution temperature is 1150-1230 ℃, preserving the heat for 1-5 h, and then cooling to room temperature at a cooling speed of not less than 300 ℃/min. And carrying out aging treatment on the material subjected to the solution treatment, wherein the aging temperature is 600-750 ℃, keeping the temperature for 2-50 h, and then air-cooling to room temperature.
The present invention will be described in detail with reference to specific examples.
Table 1 shows the chemical compositions in percentage by mass of the examples and comparative examples of the present invention, Table 2 shows the manufacturing processes of the steel grades of the examples and comparative examples of the present invention, and Table 3 shows the linear expansion coefficient α of the steel grades of the examples and comparative examples of the present inventionm(25,400)Room temperature hardness, and room temperature hardness after heat preservation at 700 ℃ for 24 h.
The content ratios of the components in examples 1 to 11 and comparative examples 1 to 2 were designed as shown in Table 1.
TABLE 1 (unit: wt%)
Figure BDA0002753469270000151
Figure BDA0002753469270000161
The steel materials having the compositions shown in table 1 were made into a cast slab after smelting and casting. Heating the casting blank at the heating temperature of 1130 ℃, preserving heat for 4 hours, and finishing hot working deformation under the condition that the pass temperature is not lower than 880 ℃. The hot working modes, the ratios of the original casting blank cross-sectional areas to the final plate/bar cross-sectional areas of the examples and comparative examples are shown in table 2, and the hot-worked bars or plates are subjected to the heat treatment process shown in table 2 to obtain the final bars or plates.
TABLE 2
Figure BDA0002753469270000162
Figure BDA0002753469270000171
Linear expansion coefficient alpha of inventive examples 1 to 11 and comparative examples 1 to 2m(25,400)The room temperature hardness and the room temperature hardness after heat preservation at 700 ℃ for 24 hours are shown in Table 3.
TABLE 3
Figure BDA0002753469270000172
As can be seen from Table 3, the present invention can obtain high strength austenitic alloy steel with high expansibility and thermal stability by reasonable composition and process design, and the coefficient of linear expansion alpha thereofm(25,400)≥16.5×10-6The room temperature hardness of the alloy steel is not less than 36HRC, and the room temperature hardness is not less than 34HRC after heat preservation is carried out for 24 hours at 700 ℃.
The embodiments described above are described to facilitate an understanding and use of the invention by those skilled in the art. It will be readily apparent to those skilled in the art that various modifications to these embodiments may be made, and the generic principles described herein may be applied to other embodiments without the use of the inventive faculty. Therefore, the present invention is not limited to the above embodiments, and those skilled in the art should make improvements and modifications within the scope of the present invention based on the disclosure of the present invention.

Claims (10)

1. A precipitation hardening austenitic alloy steel with high expansibility and thermal stability is characterized by comprising the following chemical components in percentage by mass: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent.
2. The precipitation hardening austenitic alloy steel with high expansibility and thermal stability according to claim 1, wherein the precipitation hardening austenitic alloy steel with high expansibility and thermal stability contains the following elements in percentage by mass: c is more than or equal to 0.45 percent and less than or equal to 0.65 percent, Cr is more than or equal to 9.0 percent and less than or equal to 12.0 percent, Mo is more than or equal to 1.5 percent and less than or equal to 3.0 percent, Cu is more than or equal to 1.5 percent and less than or equal to 3.0 percent, V is more than or equal to 0.8 percent and less than or equal to 1.2 percent, and Nb is more than or equal to 0.15 percent and.
3. The precipitation hardenable austenitic alloy steel with high expansion and thermal stability according to claim 1, wherein the matrix structure of the precipitation hardenable austenitic alloy steel with high expansion and thermal stability is a single austenitic structure and second phase particles dispersed in the austenitic matrix;
the second phase particles are mainly MX type carbides and carbonitrides formed between C element and V, Nb element and carbides formed between C element and Cr element.
4. The precipitation hardened austenitic alloy steel with high expansion and thermal stability according to claim 1, wherein the physical and mechanical properties of the precipitation hardened austenitic alloy steel with high expansion and thermal stabilitySatisfies the following conditions: coefficient of linear expansion alpham(25,400)≥16.5×10-6The room temperature hardness is not less than 36HRC, and the room temperature hardness is not less than 34HRC after heat preservation is carried out for 24 hours at 700 ℃.
5. A method of manufacturing a precipitation hardening austenitic alloy steel with high expansion and thermal stability according to any of claims 1-4, characterized by the steps of:
1) smelting and casting according to the following component proportion to obtain a casting blank
The mass percentage of the chemical components is as follows: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent;
2) thermal deformation processing
Heating a casting blank at 1050-1230 ℃, preserving heat for 1-6 hours, and then thermally processing the casting blank into a bar or a plate;
3) post-deformation heat treatment
The post-deformation heat treatment comprises two procedures of solution treatment and aging treatment, wherein the solution treatment is firstly carried out on the bar or plate after the hot working deformation, and then the aging treatment is carried out on the material after the solution treatment.
6. A method of manufacturing a precipitation hardening austenitic alloy steel with high expansion and thermal stability according to any of claims 1-4, characterized by the steps of:
1) smelting and casting according to the following component proportion to obtain a casting blank
The mass percentage of the chemical components is as follows: c is more than or equal to 0.35 percent and less than or equal to 1.0 percent, Mn is more than or equal to 3.0 percent and less than or equal to 15.0 percent, Si is less than or equal to 3.0 percent, Al is less than or equal to 3.0 percent, Cr is more than or equal to 7.0 percent and less than or equal to 15.0 percent, Ni is more than or equal to 2.0 percent and less than or equal to 10.0 percent, Mo is more than or equal to 0.5 percent and less than or equal to 4.0 percent, Cu is more than or equal to 0.5 percent and less than or equal to 4.0 percent, V is more than or equal to 0.4 percent and less than or equal to 2.0 percent, Nb is more than or equal to 0.; wherein, the mass percentages of Nb and V elements also need to satisfy the following relations: 0.65 percent to 0.7 percent of Nb + V and 2.5 percent to less; the mass percentages of Si and Al elements also need to satisfy the following relations: al and Si are more than or equal to 0.8 percent and less than or equal to 4.0 percent;
2) thermal deformation processing
The hot working comprises two parts of forging cogging and hot rolling, wherein the forging cogging treatment is firstly carried out, and then the hot rolling treatment is carried out;
3) post-deformation heat treatment
The post-deformation heat treatment comprises two procedures of solution treatment and aging treatment, wherein the solution treatment is firstly carried out on the bar or plate after the hot working deformation, and then the aging treatment is carried out on the material after the solution treatment.
7. The method of manufacturing a precipitation hardening type austenitic alloy steel having high expansibility and thermal stability according to claim 5, wherein the hot deformation mode in the step 2) is hot rolling or forging, the pass temperature is not less than 850 ℃, and the ratio of the cross sectional area of the cast slab before and after hot deformation is not less than 2.0.
8. The method of manufacturing a precipitation hardening austenitic alloy steel having high expansibility and thermal stability according to claim 6, wherein the conditions for forging and cogging in the step 2) are: heating a casting blank at 1050-1230 ℃, preserving heat for 1-6 h, forging the casting blank into a plate blank or a square blank, wherein the forging deformation pass temperature is more than or equal to 850 ℃, and the ratio of the cross sectional areas of the casting blank before and after forging is more than or equal to 1.5;
the conditions for hot rolling treatment were: heating the forging blank at 1050-1230 ℃, preserving heat for 1-6 h, and then hot-rolling the forging blank into a plate or a bar, wherein the hot-rolling deformation pass temperature is not less than 850 ℃, and the ratio of the cross-sectional area of the original casting blank to the cross-sectional area of the hot-rolled plate or bar is not less than 2.0.
9. The method for manufacturing a precipitation hardening austenitic alloy steel with high expansibility and thermal stability according to claim 5 or 6, wherein the solution treatment is performed in step 3) under the following conditions: the solid solution temperature is 1150-1230 ℃, the temperature is kept for 1-5 h, and then the mixture is cooled to the room temperature at the cooling speed of not less than 300 ℃/min.
10. Method for manufacturing a precipitation hardening austenitic alloy steel with high expansion and thermal stability according to claim 5 or 6, characterized in that, in step 3), the aging treatment is performed under the conditions: the aging temperature is 600-750 ℃, the temperature is kept for 2-50 h, and then the air cooling is carried out to the room temperature.
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CN113943849A (en) * 2021-10-18 2022-01-18 华能国际电力股份有限公司 Heat treatment process of high-chromium heat-resistant alloy
CN114645218A (en) * 2022-04-01 2022-06-21 成都成林数控刀具股份有限公司 high-C high-Ni austenitic age-hardening heat-resistant steel and preparation method thereof
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CN115287548A (en) * 2022-10-10 2022-11-04 山东瑞泰新材料科技有限公司 High-expansion alloy steel and preparation method and application thereof

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Publication number Priority date Publication date Assignee Title
CN113943849A (en) * 2021-10-18 2022-01-18 华能国际电力股份有限公司 Heat treatment process of high-chromium heat-resistant alloy
CN114645218A (en) * 2022-04-01 2022-06-21 成都成林数控刀具股份有限公司 high-C high-Ni austenitic age-hardening heat-resistant steel and preparation method thereof
CN115181900A (en) * 2022-04-01 2022-10-14 成都成林数控刀具股份有限公司 Austenite age hardening heat-resistant steel and preparation method thereof
CN115287548A (en) * 2022-10-10 2022-11-04 山东瑞泰新材料科技有限公司 High-expansion alloy steel and preparation method and application thereof
CN115287548B (en) * 2022-10-10 2023-01-17 山东瑞泰新材料科技有限公司 High-expansion alloy steel and preparation method and application thereof

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